Mater.Phys.Mech. 1 (2000) ??-??
1
AC MAGNETIC PROPERTIES OF COMPACTED FeCo
NANOCOMPOSITES
Anit K. Giri, Krishna M. Chowdary and Sara A. Majetich
Department of Physics, Carnegie Mellon University
Pittsburgh, PA 15213-3890, USA
Email: ____________________
Received November 17, 1999
Here we report the AC magnetic properties of soft magnetic
nanocomposites made from compaction of Fe10Co90 nanoparticles. Following
a discussion of previous work on soft magnetic nanocomposites, the sample
preparation and experimental characterization by AC permeametry are
described. The permeability is constant and equal to the DC value for low
frequencies, but drops off sharply above a characteristic frequency fc. A model
is developed to explore the relation between fc and material parameters
including the effective anisotropy, exchange coupled volume, temperature,
and saturation magnetization.
Abstract.
1.
INTRODUCTION
Many recent developments in soft magnets, which are used in power applications,
have been based on amorphous and nanocrystalline materials [1-5]. In amorphous solids the
magnetocrystalline anisotropy K is by definition equal to zero, eliminating the main materialdependent contribution to the coercivity. The effective anisotropy Keff can also be low in
nanocrystalline materials if conditions specified by the Random Anisotropy Model are met
[1-3, 6]. The grain size must be smaller than the magnetic exchange length Lex, and the grains
must be exchange coupled with their easy axes for magnetization randomly oriented. The
combination of random orientation and averaging over multiple grains makes the preference
for magnetization in a particular direction, and therefore Keff, very small. Theoretically, low
K materials become even softer if the grain size D is small enough. The DC magnetic
properties of nanocomposites have been modeled in terms of the Random Anisotropy Model
[1-3]. The magnetization reversal field or coercivity Hc is predicted to be proportional to D ,
while the permeability =B/H is predicted to be proportional to D. Here we extend this
approach to understand the AC magnetic properties of nanocomposites.
@ 2000 Advanced Study Center Co. Ltd.
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Aqnit K. Giri et al
Previous work on the AC magnetic properties of bulk magnetic materials has shown
that the permeability can be split into in-phase (’) and out-of-phase (”) components, just
like the permittivity of dielectric materials:
 = ’ - i”.
(1)
These components obey a Kramers-Krönig relationship [7], so that by knowing the
value of one for all frequencies, the other is uniquely determined. The real part ' is typically
flat up to a cutoff frequency, and then drops off, while the imaginary part " shows a peak at
the same frequency. In the best high frequency ferrite materials, the cutoff frequency is in the
GHz range, and is associated with the precession frequency of spins about the applied
magnetic field. While high frequency magnetic materials are highly insulating to reduce eddy
current losses, their properties have not been analyzed in terms of their microstructure.
A benchmark for soft magnetic materials is the total power loss, Ptot, as the material is
magnetized and demagnetized. It depends on the hysteresis loss, losses due to the eddy
currents created by the changing magnetic field, and anomalous losses associated with
domain wall motion [8] These contributions have different frequency dependencies:
Ptot = Phys + Peddy current + Panom = Whys f + A f2/+ Panom(f).
(2)
Phys varies linearly with the frequency f and the area within the hysteresis curve Whys,
Peddy current is quadratic in frequency and inversely proportional to the resistivity . A is a
constant. The anomalous loss Panom has no fixed power law dependence on the frequency.
The AC magnetic properties of ferrofluids, which are small (< 10 nm) magnetic
particles dispersed in a liquid, show distinctly different behavior from that of bulk materials.
There are two characteristic relaxation times, one due to Brownian relaxation caused by
rotation of the particles in the liquid, and the other due to Néel relaxation caused by coherent
rotation of the atomic spins within the particle [9,10]. Both processes occur at frequencies
well below the Larmor frequency fo.
Nanocomposites have potential for two niche applications of soft magnetic materials.
In low frequency applications, amorphous materials should continue to dominate, since they
have the smallest hysteretic losses. Without significant eddy currents, only the small
percentage of atoms required for glass forming do not contribute to the magnetization.
However, at higher temperatures amorphous materials crystallize. In the current
nanocrystalline materials [1-5], grain growth is limited by precipitation of additional phases,
and a larger fraction of nonmagnetic atoms is needed. At higher frequencies, nanocomposites
have potential advantages because they can have higher resistivity to reduce eddy current
losses. While ferrites are currently used for high frequency applications because of their high
resistivities, they have much lower magnetizations than iron-based alloys.
Iron-cobalt alloys are of interest for high temperature soft magnets because they have
a high Curie temperature, high magnetization, and low coercivity. The value of the Curie
temperature depends on the relative Co abundance. Iron-cobalt alloys have the largest
magnetic moment per atom, and therefore large saturation magnetizations [11]. They have a
low coercivity due to the low magnetocrystalline anisotropy K of the body-centered cubic
structure. There is a zero crossing of the anisotropy near the equiatomic composition [12].
3
AC Magnetic Properties
3
We investigate nanolaminates formed by compaction of FeCo nanoparticles with a
very thin coating of a protective carbon or oxide. By choosing a particle or grain diameter
well below the maximum monodomain size, the coercivity and hysteretic power losses can be
minimized [1-3]. The coatings act as a barrier to eddy currents, reducing the eddy current
power losses at high frequency. The goals are to minimize the portion of nonmagnetic atoms
while retaining a stable nanocrystalline structure at high temperature, and to determine the
degree of coating which retains significant exchange coupling for minimum Keff while
creating significant barriers to eddy currents.
2.
EXPERIMENTAL
2a.
Particle Synthesis
Here the alloy nanoparticles were synthesized by the polyol method [13], a chemical
route which leads to highly monodisperse metal particles. Iron chloride tetrahydrate and
sodium hydroxide were dissolved in ethylene glycol and heated to 110 °C while stirring. A
second solution of cobalt hydroxide in ethylene glycol at the same temperature was added,
and the mixture was heated to 195 °C, where a precipitate formed. The total metal ion
concentration was 0.2 M, and the hydroxide concentration was 2.0 M. Water and other
reaction products were distilled off, and the solvent was refluxed for one hour at the
maximum temperature. The precipitate was thoroughly washed with methanol, and dried.
While the particle size can be varied by changing the metal salt concentration and
reaction time, the average grain diameter was roughly constant and approximately 20 nm.
The composition was determined from electron energy loss spectroscopy [14]. The average
grain size was obtained from Scherrer analysis of the x-ray diffraction peaks, and the particle
size was found from transmission electron microscopy. The exchange length in magnetically
soft materials like FeCo is large, and here is comparable to the grain size. Adjacent grains can
then be exchange coupled to each other, leading to a further reduction in the anisotropy and
coercivity, as explained by the random anisotropy model [1-3, 6].
2b.
Compaction
A nanocomposite has nanoparticle-sized grains, which may be dispersed in a matrix
that mediates their coupling. The coupling strength depends on the magnetic behavior of the
matrix and on the degree of coherence at the interface between the nanoparticles and the
matrix. Exchange interactions may couple nanoparticles together. We worked with Dr. S.
Sudarshan and Mr. Sang Yoo of Materials Modification, Inc., on plasma pressure
compaction, which has the advantage of being able to reduce or remove the thin coating
surrounding FeCo nanoparticles under ambient conditions. Powders were compacted by a
combination of pressure and an electric arc in a two stage process. First a voltage pulse
established a continuous current path across the sample in a graphite mold under a pressure of
10 MPa. This generated a plasma in the voids, and partly removed surface impurities such as
oxides. In the second stage a continuous current path led to resistive sintering. The pressure
was increased to 70 MPa to deform and compact the particles. The entire process required
only a few minutes, thereby limiting grain growth. The resistive heating concentrated in the
“necks” forming as the particles sinter, making them deform more readily. Compacts with
over 90% theoretical density were made from the nanoparticle powders.
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2c.
Magnetic Properties
There was a substantial amount of magnetic characterization, including SQUID
magnetometry (with a Quantum Design MPMS) to determine the coercivity, and AC
permeametry (with a Walker Scientific AC Hysteresisgraph) on toroidal compacts to measure
the frequency dependence of the permeability  and the power loss. For the AC
measurements, the toroid outer diameter was 2.54 cm, and it had a square cross section with
dimensions 3.0  4.1 mm. There were 154 primary turns and 11 turns in the pickup coil. The
amplitude of the AC magnetic field applied was 125 Oe, and the frequency ranged from 100
to 100,000 Hz. The temperature of the toroid was controlled by placing it in thermal contact
with an ice bath (0°C), or with it inserted in a furnace (100 °C - 500 °C). At elevated
temperatures the coils were sheathed with fiberglass sleeving (Omega Engineering, Inc.).
3.
EXPERIMENTAL RESULTS
100
20 b)
a)
M (emu/g)
M (emu/g)
Fig. 1 shows a comparison of the DC hysteresis loops for the powder and compacted
pellet of a typical sample. Compaction significantly reduces the coercivity, indicating that the
exchange coupling is increased, as predicted by the random anisotropy model.
0
-100
-50
-25
0
25
3
H (10 Oe)
50
10
0
-10
-20
-200
-100
0
100
H (Oe)
200
Fig. 1. a.) Comparison of Fe10Co90 nanoparticles made by the polyol method, and a compact
made from them; b.) An expanded region shows the coercivity of the pellet is on the order of
5 Oe, much less than that of the precursor particles, which is approximately 150 Oe.
The AC hysteresis loops were measured for toroids cut from the same compressed
pellets, for a range of frequencies. With AC excitation, the pickup loop measures the
magnetic induction B= 4M+H. Fig. 2 illustrates the characteristic behavior as a function of
frequency. At low frequencies (Fig. 2a) the applied field H was sufficient to saturate the
sample, reaching the single-valued region of B(H). As the frequency was raised, the width of
the hysteresis loop and therefore the coercivity increased, but the maximum induction
remained approximately the same, up to a characteristic frequency (Fig. 2b). Approaching
this frequency, the sample was no longer saturated at the maximum applied field, and the
maximum magnetic induction dropped (Fig. 2c).
5
AC Magnetic Properties
5
10
B (kG)
5
a
b
c
0
-5
-10
-120
-80
-40
0
H (Oe)
40
80
120
Fig. 2. AC Hysteresis loops for Fe10Co90, at 0 °C. a.) 100 Hz, b.) 800 Hz, c.) 5000 Hz.
The permeability as a function of the maximum applied field is illustrated in Fig. 3,
for several representative frequencies. Defining the permeability as the maximum value of
B/H, it is expected to very depending on the magnitude of Hmax. If Hmax is small and the
sample is not saturated, B increases approximately linearly with H, and  is large. If Hmax is
large and the sample is never saturated, B increases more slowly with increasing H and  is
reduced. In order to understand the fundamental physics of the AC excitation of the
nanocomposites, a value of Hmax = 125 Oe was selected for further measurements so that the
samples were saturated at low frequency.
300
f = 500 Hz
f = 900 Hz
f = 1400 Hz
250

200
150
100
50
0
20
40
60
80
Hmax (Oe)
100
120
Fig. 3. Overall permeability for Fe10Co90, as a function of Hmax, at 0 °C, for 500, 900, and
1400 Hz. The peak permeability at 22 Oe reflects where the slope of the B(H) starts to
decrease.
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Aqnit K. Giri et al
Several important quantities for soft magnetic materials were measured as a function
of frequency. The real (in-phase) and imaginary (out-of-phase) parts of the permeability
=B/H were also measured as a function of frequency (Fig. 4). In the low frequency range,
the phase lag between B and H is small, and " is negligible. ' is roughly constant up to the
characteristic frequency, where it drops off sharply. " peaks as ' drops off, and the critical
frequency fc is determined from the position of the peak in ". The characteristic frequency of
the permeability varied with temperature (Fig. 5). While the low frequency magnitude of 
dropped off slightly with increasing temperature, due to a reduction in the magnetization, fc
rose substantially, from 1400 Hz at 0 ° C to 6000 Hz at 500 ° C. As noted in the hysteresis
loops, the coercivity rose with increasing frequency (Fig. 6). It peaked at a frequency
approximately 2-3 times fc, and decreased somewhat at high frequencies. The overall power
loss per cycle is shown in Fig. 7. At low frequencies it rises linearly, as expected from Eq. 2
if hysteretic losses are dominant. At frequencies above fc a weaker dependence is observed,
closer to f0.5. As the temperature is increased the power loss per cycle decreases somewhat,
due mainly to the reduction in the coercivity.
100
'
''
', ''
80
60
40
20
0
10
2
10
3
f (Hz)
10
4
10
5
Fig. 4. The real (’) and imaginary (” ) parts of the permeability for Fe10Co90, at 0 °C, as a
function of frequency.
7
AC Magnetic Properties
7
120
o
0 C
o
500 C
100
80

60
40
20
0
10
2
10
3
f (Hz)
10
4
10
5
Fig. 5. Overall permeability as a function of frequency for Fe10Co90, at 0 °C and 500 °C.
100
Hc (Oe)
80
60
40
o
0 C
o
500 C
20
0
10
2
10
3
f (Hz)
10
4
10
5
Fig. 6. Coercivity as a function of frequency for Fe10Co90, at 0 °C and 500 °C.
P (W/cc)
100
10
1
2
10
3
10
f(Hz)
10
4
5
10
Fig. 7. Power Loss per unit volume as a function of frequency for Fe10Co90, at 0 °C.
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Aqnit K. Giri et al
4. MODEL OF AC MAGNETIC PROPERTIES
Our model of the AC properties of nanocomposites is based on a monodomain
magnetic particle in an oscillating magnetic field. For a uniaxial particle with the applied
field parallel to the easy axis, the energy E is given by
2
E  KV sin   Ms H cos 
(3)
where K is the magnetocrystalline anisotropy, V is the particle volume,  is the angle between
the magnetization direction and the applied field H, and Ms is the saturation magnetization.
Stoner-Wohlfarth theory [15-17] has shown that energy minima occur at  = 0° or 180°, and a
maximum exists where cos=-HMs/2K. In order to reverse the magnetization direction, the
energy barrier must be overcome. If this does not occur within the measurement time, then
hysteresis is observed. The rate of going over the barrier o-1 is given by
E 
,
 kT 
 1   01 exp 
(4)
where o-1 = f0 is the Larmor frequency, E is the magnitude of the energy barrier, k is the
Boltzmann constant, and T is the temperature.
If the magnetic field oscillates in time,
H(t)  H0 cos(2 ft) ,
(5)
then the positions of the energy minima and maxima will also change with time, as shown in
Fig. 8. Early in the cycle state 1 is the global minimum and state 2 is a local minimum, but
later the roles are reversed. The height of the energy barrier which must be overcome for the
particle to switch from the local to the global minimum also oscillates in time and is greatest
at zero applied field.
2ft=
2ft=0
E
E bkwd
2ft=2
Efwd
E=KV
2
1
1
2M sHV
2
1
2
2MsHV
Time
Fig. 8. Energy levels as a function of time, for different parts of the cycle of H(t). Here E1 is
the energy of a particle in state 1, E2 is the energy of a particle in state 2, and E is the
magnitude of the barrier between the local minimum and the maximum energy states.
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AC Magnetic Properties
9
Given an ensemble of particles and monitoring the population N1 in state 1 and N2 in
state 2 as a function of time, the magnetization can be determined:
M(t )  Ms ( N1(t )  N2 (t ))  Ms (2N1 (t) 1) .
(6)
Here we assume that population is conserved, and that at all times
N1  N2  1 .
(7)
The population in state 1 as a function of time depends on the rate bkwdat which
particles get over the barrier from state 2, and on the rate fwdthat they leave state 1 in the
forward direction over the barrier:
dN1
dN
1
1
  2   bkwd N2   fwd N1 .
dt
dt
(8)
Substituting for the rates using Eq. 4,

dN1
 E fwd 
 Ebkwd 
  01 (1 N1 )exp 
 N1 exp 
.
dt
 kT

 kT 

(9)
Substituting for the forward Efwd and reverse Ebkwd energy barriers,
2
 HM s 
E fwd  Emax  E1  KV 1 

2K 

(10a)
2
 HM s 
,
Ebkwd  Emax  E2  KV 1

2K 

(10b)
the differential equation becomes

 KV  HM 2 
KV
dN1
1
s
  0 1 N1 exp 
1
  N1 exp 


dt
2K  

 kT 
 kT

2
 HM s  
1


 2K 
 
.
(11)
In an oscillating magnetic field H(t), Eq. 11 must in general be solved numerically.
This problem has many similarities to that of an electric dipole in an AC electric field,
which was originally solved by Peter Debye [18,19], with two main differences. In the
electric dipole model, there was no equivalent to magnetocrystalline anisotropy, so the
solution corresponds to the superparamagnetic limit. Also, in the electric dipole model, the
factor equivalent to x = MsVH/kT is much less than one, and when ex is approximated by
1+x, the equation corresponding to Eq. 11 can be solved analytically.
Equation 11 can be solved analytically in the limit of large K, where E fwd  Ebkwd .
With the substitution
y
KV
kT
,
(12)
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Aqnit K. Giri et al
Eq. 11 then simplifies to
dN1
1 y
  0 e (1 2N1 ) .
dt
(13)
The solution to Eq. 13 is given by
N1 (t ) 

.
1
1
1 exp(2 0 yt )
2
(14)
There will be a characteristic or resonant frequency fc, where
fc 
y
 1   KV 
 1
0 e
,
  0 exp 

    kT 
(15)
where the population oscillates in resonance with the driving field H(t). Above this
frequency, the population shifts cannot keep up with the rapidly changing driving field.
The model breaks down for cases where HMs/2K > 1, since this requires that |cos=HMs/2K| be greater than one. To investigate the small K limit, which is of critical importance
for soft magnetic materials, we reduced the amplitude of the magnetic field Ho where
necessary. In experiments it is possible to have large amplitudes of the AC magnetic field
when studying materials with very low anisotropy. Here the sample is being driven past the
high slope portion of the hysteresis curve during each half-cycle. In applications of soft
magnetic materials, this is undesirable since the permeability =B/H is reduced. Therefore the
model can be used to understand the AC magnetic behavior in situations of greatest
technological importance.
5. MODELING RESULTS AND COMPARISON WITH EXPERIMENT
The simulation results show the same characteristics as the experimental data, and
provide insight about the mechanism responsible for the frequency dependent behavior.
Fig. 9 illustrates the connection between the time-dependence of M and the B(H) curves for
driving fields of different frequencies H=Hocos(2ft). If the frequency is low enough (Fig. 9a)
the sample has time to equilibrate with the slowly varying field and superparamagnetism is
observed. There is a negligible phase lag  between M(t) and H(T). Because of this M(t)
reaches its maximum value well below the maximum amplitude of the driving field Ho. At
somewhat higher frequencies M(t) starts to lag behind H(t) significantly, leading to hysteresis
(Fig. 9b) . However M(t) still reaches its maximum value before H(t) starts to decrease. At
the critical frequency fc this is no longer true (Fig. 9c), and the shape of M(t) and the
hysteresis loop change noticeably. B(H) no longer contains single valued regions, and the
maximum value of B starts to decrease relative to its value at lower frequencies. At the
highest frequencies M(t) and H(t) are almost completely out of phase and the maximum
values of M(t) and B(H) are very small (Fig. 9d). The model simulates characteristics of the
experimental results shown in Fig. 2, and shows that the shape and magnitude of B(H)
depend on whether the magnetization of the exchange coupled volume within the sample can
equilibrate with the changing external magnetic field.
11
AC Magnetic Properties
H(t)
M(t)
a)
11
B (Gauss)
f = fc x 10 -6
 = 0.4o
superparamagnetic
t(s)
b)
f = fc x 10-1
 = 23.0o
c)
f = fc
 = 69.8o
d)
H (Oe)
Hysteresis when
M(t) lags H(t)
Bmax drops
increases
f = fc x 101
 = 86.1o
Fig. 9. M(t) and H(t), and the corresponding B(H) curves for a sphere of exchange coupled
volume V and effective anisotropy K. a.) for a superparamagnetic particle, b.) for a
monodomain but not superparamagnetic particle at low frequency f, c.) at med. f, and d.) at
high f. Note that in a.) and b.) B(H) appears to saturate, but this is because 4M is so much
larger than H. These simulations used the following parameters: Ms = 1000 emu/cc, H0 = 125
Oe, K = 1.95 105 erg/cc, T=273 K, and V = 1.47 10-18 cc. The critical frequency fc was
1400
Hz.
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Aqnit K. Giri et al
Figure 10 shows the corresponding trend in the permeability  as a function of
frequency. At low frequencies it is constant and equal to the DC value, but as soon as M(t) is
unable to reach its maximum value, Bmax and therefore  begin to drop, approaching zero in
the high frequency limit. This is in contrast to the experimental results shown in Fig. 5, where
 decays more slowly. Such a difference would arise if the sample contained a distribution of
characteristic frequencies fc, perhaps related to a distribution of grain sizes.
100

80
60
40
20
0
101
102
103
Frequency (Hz)
104
Fig. 10. The permeability =Bmax/Hmax as a function of frequency, for the same parameters as
in Fig. 9.
Fig. 11 reveals the behavior of the simulated coercivity as a function of frequency. At
low frequencies it follows Sharrock’s Law [20]:
1/ 2
2K  kT ln f 0 / f  
Hc ( f )   1  
 
KV
 Ms 

 

,
or
  2K  kT 1/ 2 1 
2K   kT 1/2 1 
  ln f
Hc ( f )   1     ln f 0   
 Ms  KV  2 
  M s  KV  2 
,
(16a)
(16b)
rising with the log of the frequency. The peak in Hc occurs between two and three times fc,
and then Hc begins to decrease. This occurs when the magnetization due to the driving field is
low enough, and the value of H(t) needed to make M(t) equal to zero is reduced. The
experimental coercivity shown in Fig. 6 also rises and peaks at roughly the same frequency,
but the rise is not proportional to ln f. While there may be a region where Hc obeys this
functional dependence, there appears to be a low frequency contribution to the coercivity
from a factor not included in the model. This could arise from particles not exchange coupled
to their neighbors, possibly from a thicker coating.
Fig. 12 shows the hysteretic power loss Phys found from the are of the hysteresis loop
B(H), as a function of frequency. This rises linearly at low frequencies, as expected from Eq.
2, but then it levels off at fc. At very high frequency it should decrease when both Mmax and
Hc are decreasing.
13
AC Magnetic Properties
13
In comparison, Fig. 7 shows the total experimental power loss. At frequencies below
fc, hysteretic power losses dominate. This is expected for frequencies below 10,000 Hz.
Coercivity (Oe)
120
100
80
60
0
10
1
2
10
10
3
10
4
10
5
10
6
10
Frequency (Hz)
Fig. 11. The coercivity Hc as a function of frequency, for the same parameters as in Fig. 9.
5
Hysteretic Power Loss
10
104
3
10
101
102
103
Frequency (Hz)
104
Fig. 12. The hysteretic power loss as a function of frequency, for the same parameters as in
Fig. 9.
The qualitative behavior illustrated in Fig. 9-12 is similar for a wide range of input
parameters; only the magnitudes of , Hc and Phys vary, along with the critical frequency fc.
The dependence of fc on the anisotropy, volume, and temperature is summarized in Fig. 13.
From the simulated data, an empirical functional form for fc(K,V,T) was obtained:
f c  10

9 1
 0 exp (5.88  1015 K


 KV 
V 
6
20
/ erg)   (4.33 10 cc / erg)K  (4.11 10 K / cc)   18.98 (17)
 T 
 T 

Note that this formula is considerably more complex than Eq. 15, which was valid only in the
limit of large K. For soft magnetic materials K is small, and numerical simulations are the
only was to predict the cutoff frequency.
14
Aqnit K. Giri et al
Cutoff Frequency (Hz)
14
8
10
106
4
10
2
10
r = 7 nm
r = 10 nm
r = 12 nm
0
10
T = 273 K
-2
10
50
100
5
10
5
K = 1x10 (ergs/cc)
0
10
K = 1.5x10
5
2
3
b.)
Cutoff Frequency (Hz)
5
(ergs/cc)
K = 2x10 (ergs/cc)
1
c.)
300x10 3
200
Anisotropy (ergs/cc)
a.)
Cutoff Frequency (Hz)
150
4
T = 273 K
5
Volume (cc)
6
8x10
-18
8
10
7
10
6
10
(KV)1 = 6.42 x 10
5
(KV)2 = 1.44 x 10
10
(KV)3 = 2.88 x 10
4
10
0
1
2
-14
-13
-13
ergs
ergs
ergs
3
4
-1
1/Temperature (K )
5x10
-3
Fig. 13 a.) fc as a function of the anisotropy for spheres of different radii. Here V=(4/3) r3;
b.) fc as a function of the volume; c.) fc as a function of the inverse temperature.
15
AC Magnetic Properties
15
For the experimental grain size, r=10 nm, and an effective anisotropy equal to 1.5 
105 erg/cc would be needed to fit the observed room temperature value of fc. The is a much
larger value of the anisotropy estimated from the experimental coercivity and Sharrock’s
Law. Presumably the physically relevant volume V is not that of a single grain, but of a small
number of coupled grains.
6.
CONCLUSIONS
The AC magnetic properties of soft magnetic nanocomposites made from compaction
of Fe10Co90 nanoparticles can be understood in terms of an effective anisotropy and a related
exchange coupled volume. The permeability is constant and equal to the DC value for low
frequencies, but drops off above a characteristic frequency fc. For bulk materials such as
ferrites the cutoff frequency can be extremely high, and the behavior is understood in terms
of the Landau-Lifshitz-Gilbert equation [21-23]. However for compacted nanocomposites the
cutoff frequency is much lower, and depends on the sample microstructure. The value of this
frequency can be increased by raising the temperature, or by reducing the anisotropy and
grain size. Experiments are in progress to prepare samples to further test this model.
7.
ACKNOWLEDGMENTS
This work was supported in part by the National Science Foundation under Grant
numbers DMR-9900550 and ECD-8907068, and by the Air Force Office of Scientific
Research under grant number F49620-96-1-0454. The assistance of K. Humfeld and N. Ide in
the simulations is greatly appreciated.
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